CN114717453A - High-toughness cast aluminum-silicon alloy and preparation method thereof - Google Patents

High-toughness cast aluminum-silicon alloy and preparation method thereof Download PDF

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CN114717453A
CN114717453A CN202210648618.3A CN202210648618A CN114717453A CN 114717453 A CN114717453 A CN 114717453A CN 202210648618 A CN202210648618 A CN 202210648618A CN 114717453 A CN114717453 A CN 114717453A
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melt
alloy
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powder
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CN114717453B (en
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樊振中
陆政
李大奎
刘闪光
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AECC Beijing Institute of Aeronautical Materials
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AECC Beijing Institute of Aeronautical Materials
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C22C1/026—Alloys based on aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C22C1/03—Making non-ferrous alloys by melting using master alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/20—Recycling

Abstract

Compared with the traditional ZL101 and ZL114 cast aluminum-silicon alloy materials, the high-strength and high-toughness cast aluminum-silicon alloy provided by the invention has the advantages that Al-Ti-C-CuO mixed powder is added in the preparation process of the high-strength and high-toughness cast aluminum-silicon alloy, and a large amount of TiC ceramic particles with small and uniform sizes are generated in a melt through reaction; the eutectic silicon phase is fully and effectively modified by virtue of Eu and La rare earth elements, the morphology of the silicon phase can be changed from a plate shape and a needle shape into a spherical shape, the stress concentration degree of the tip of the silicon phase is greatly reduced, and the plasticity and toughness of the material are improved. The high-toughness preparation of the alloy material can be realized, the short-period low-cost casting of the precision aluminum alloy casting with the complex structure of the military equipment can be realized, and the economic benefit is obvious.

Description

High-toughness cast aluminum-silicon alloy and preparation method thereof
Technical Field
The invention belongs to the field of casting and colored casting alloy materials, and particularly relates to a high-strength and high-toughness casting aluminum-silicon alloy and a preparation method thereof.
Background
The aluminum alloy has the advantages of low density, high specific strength/rigidity, good corrosion resistance, good plasticity, excellent processing performance, good welding performance, excellent electrical conductivity and thermal conductivity, and is widely applied to the field of military equipment. The aluminum alloy can be mainly divided into wrought aluminum alloy and cast aluminum alloy according to the processing technology, wherein the cast aluminum alloy has good process flow property and medium load bearing capacity, and is widely applied to the manufacture of products such as missile shells, oil-carrying cabin shells, engine accessory casings, engine oil-way pipelines, automobile engine cylinder bodies, automobile engine cylinder covers and the like.
The cast aluminum alloy which is most widely applied in the prior art is mainly cast aluminum-silicon alloy, the dosage of the cast aluminum-silicon alloy accounts for more than 70 percent of the total dosage of the cast aluminum alloy, and the dosage of two cast aluminum-silicon alloys of ZL101 and ZL114 in the cast aluminum-silicon alloy is the most, and the cast aluminum-silicon alloy accounts for more than 80 percent of the total dosage of the cast aluminum-silicon alloy. The tensile strength of ZL101 cast aluminum-silicon alloy is about 240MPa generally, the average elongation is 4-6%, and the ZL101 cast aluminum-silicon alloy is widely applied to the civil and automobile manufacturing fields of manufacturing automobile hubs, engine cylinder bodies, engine cylinder covers, new energy automobile die castings and the like; the tensile strength of ZL114 cast aluminum-silicon alloy can reach about 320MPa, the average yield strength is about 260MPa, the elongation is about 5 percent generally, and the aluminum-silicon alloy is mainly used for manufacturing missile shells, oil-carrying cabin sections, airplane cabin frameworks and other military equipment fields.
With the continuous improvement of the weight reduction technical index requirements of the automobile and weapon equipment structure, on the premise of improving the strength and toughness of the cast aluminum-silicon alloy in service, the weight of a workpiece can be reduced through structural optimization design, and lightweight design and manufacturing are realized; therefore, research on the preparation process of the novel cast aluminum-silicon alloy is developed, the component design and the optimization of the heat treatment process of the novel cast aluminum-silicon alloy are completed, and the high strength and toughness, low cost and short-period manufacturing of the aluminum-silicon alloy casting with the complex structure are imperative.
Disclosure of Invention
Researches find that the implementation process of the high-strength and high-toughness preparation of the cast aluminum-silicon alloy mainly comprises silicon phase modification, grain refinement and melt purification treatment, the quantity and the severity of metallurgical defects in a casting can be reduced through the melt purification treatment, and the strength of the alloy material is effectively improved; the silicon phase deterioration can effectively improve the appearance, size, orientation and distribution of eutectic silicon phase, regulate and control silicon phase particles with fine size, uniform distribution and similar spheroidization appearance, reduce the stress concentration degree of a silicon phase tip region and improve the ductility and toughness of an alloy material; the grain refinement is the only preparation process which can simultaneously improve the strength and the ductility and toughness of the metal material at present, and the Hall-Petch formula can know that the material strength continuously rises along with the continuous refinement of the grain size, the finer the grain size is, the higher the mismatching degree of the grain boundary quantity and the grain boundary is, and the ductility and toughness of the metal material can be effectively improved by means of a grain boundary strengthening action mechanism. The grain refinement is an important means for improving the comprehensive performance of the material and developing a new material, and is a composite process of the material, and an In-situ Synthesis technology (In-situ Synthesis Method) can provide effective crystal nuclei for a melt, and can generate a large amount of micro ceramic particles with small size and uniform dispersion distribution In the melt while promoting the grain refinement, and the micro ceramic particles are separated out from a grain boundary In the crystal, so that the strength and the hardness of the material are improved. Compared with the traditional preparation technology of externally enhanced MMCs, the in-situ chemical reaction has obvious advantages. The interface of the reinforcement body of the in-situ synthesis reaction is clean, the wettability with the matrix is good, the interface bonding strength is high, and the proper and clean interface of the reinforcement body is more beneficial to heterogeneous nucleation. The reinforcement generated by the in-situ synthesis reaction has smaller size, more uniform distribution and obviously improved reinforcement effect. The micro-ceramic reinforcement generated by the in-situ reaction has good thermal stability in a matrix, can improve the high-temperature service capacity of the material, and is relatively simple in preparation process, low in cost and suitable for batch production and manufacturing.
In order to improve the strength and toughness of the existing ZL101 and ZL114 traditional cast aluminum-silicon alloy material, the invention screens alloy components and weight ratio, TiC ceramic particles with small size and uniform distribution are generated in a melt through in-situ chemical reaction, La and Eu elements are added to effectively modify an eutectic silicon phase, melt grain refinement treatment is completed by combining Al-2Sc intermediate alloy, Al-4Zr intermediate alloy and Al-5Ti-B intermediate alloy, the purity of the alloy melt is further improved by blowing degassing and deslagging and adding trace Li elements, and the alloy melt can be used for manufacturing high-toughness, short-period and low-cost precision aluminum alloy castings with complex structures of military equipment.
The purpose of the invention is realized by the following technical scheme:
a cast aluminum-silicon alloy comprises the following components in percentage by weight:
7-9% of Si, 0.6-0.9% of Mg, 0.18-0.30% of Sc, 0.20-0.36% of Zr, 0.12-0.20% of Eu, 0.15-0.25% of La, 0.14-0.22% of Ti, 0.04-0.08% of Li, 0.02-0.06% of C and the balance of Al and inevitable impurities.
According to an embodiment of the invention, the cast aluminium-silicon alloy has high strength and high ductility and toughness.
According to an embodiment of the invention, the cast aluminium-silicon alloy comprises the following components in weight percent: si 7% -9% (e.g., 7%, 7.2%, 7.5%, 7.8%, 8%, 8.2%, 8.5%, 8.8%, or 9%), Mg 0.6% -0.9% (e.g., 0.6%, 0.65%, 0.70%, 0.75%, 0.80%, 0.85%, or 0.90%), Sc 0.18% -0.30% (e.g., 0.18%, 0.20%, 0.22%, 0.24%, 0.25%, 0.26%, 0.28%, or 0.30%), Zr 0.20% -0.36% (e.g., 0.20%, 0.22%, 0.25%, 0.28%, 0.30%, 0.32%, 0.35%, or 0.36%), Eu 0.12% -0.20% (e.g., 0.12%, 0.14%, 0.15%, 0.16%, 0.18%, or 0.2%), 0.15%, 0.25%, 0.15%, 14%, or 0.15%, 15%, 0.15%, or 0.15%, or 0.9%, 0.0.9%, 0.9%, 0.0.0.0.0.0.9%, 0.0.9%, 0.9%, 0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.25%, 0.0.0.75%, 0.0.0.0.0.0.0.0.0.0.0.0.0.0.25%, 0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.75%, 0.0.0.0.0.0.0.0.25%, 0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.0.75%, 0.0.0.0.0.0.0.0.0.0.0.0.0.25%, 0.0.0.25%, 0.0.0.75%, 0.0.0.0.0.0.0.0.75%, 0.0.0.0.0.0.0.0.0.0.0, 0.02-0.06% (e.g., 0.02%, 0.03%, 0.04%, 0.05% or 0.06%) C, and the balance Al.
According to an embodiment of the invention, the cast aluminium-silicon alloy comprises the following composition in weight percent: b is 0-0.02%. The B element and the Ti element form TiB in the alloy2And can be used as a grain refining crystal core.
According to an embodiment of the invention, the cast aluminium-silicon alloy comprises the following components in weight percent: 0-0.02% of Cu.
According to the embodiment of the invention, the tensile strength of the cast aluminum-silicon alloy is 340-380 MPa (the test standard is GB/T228.1-2010 part 1 of the tensile test of metal materials: room temperature test method), testThe test temperature was room temperature and the extensometer strain rate was 10-4 s-1～10-3 s-1) For example, 340MPa, 350MPa, 360MPa, 370MPa or 380 MPa.
According to the embodiment of the invention, the yield strength of the cast aluminum-silicon alloy is 280-320 MPa (the test standard is GB/T228.1-2010 part 1 of the tensile test of the metal material: room temperature test method, the test temperature is room temperature, the strain rate of an extensometer is 10-4 s-1～10-3 s-1) For example, 280MPa, 290MPa, 300MPa, 310MPa or 320 MPa.
According to the embodiment of the invention, the cast aluminum-silicon alloy has the elongation of 6-10% (the test standard is GB/T228.1-2010 metal material tensile test part 1: room temperature test method, the test temperature is room temperature, the strain rate of the extensometer is 10-4 s-1～10-3 s-1) For example 6%, 7%, 8%, 9% or 10%.
According to the embodiment of the invention, the Brinell hardness of the cast aluminum-silicon alloy is 120 HBS-140 HBS (test standard GB/T228.1-2010 Metal Material tensile test part 1: Room temperature test method, test temperature is room temperature, strain rate of an extensometer is 10-4 s-1～10-3 s-1) For example, 120HBS, 125HBS, 130HBS, 135HBS or 140 HBS.
The invention also provides a preparation method of the cast aluminum-silicon alloy, which comprises the following steps:
1) mixing and smelting the refined aluminum ingot, Al-12Si intermediate alloy, Al-10La intermediate alloy, Al-5Eu intermediate alloy, Al-2Sc intermediate alloy, Al-4Zr intermediate alloy and Al-Ti-C-CuO mixed powder;
2) adding a deslagging agent and a degassing agent into the melt obtained in the step 1), and degassing and deslagging;
3) adding Al-5Ti-B intermediate alloy into the melt obtained in the step 2) for secondary refining treatment;
4) adding a pure magnesium ingot and a pure lithium ingot into the melt obtained in the step 3), and then carrying out blowing degassing and standing treatment;
5) casting the melt obtained in the step 4), and then carrying out electromagnetic induction heating short-time heat treatment to prepare the cast aluminum-silicon alloy.
According to the embodiment of the invention, in the step 1), the purity of the refined aluminum cast ingot is more than or equal to 99.99%.
According to an embodiment of the present invention, in step 1), the Al-12Si master alloy, the Al-10La master alloy, the Al-5Eu master alloy, the Al-2Sc master alloy, and the Al-4Zr master alloy are commercially available products in the art.
According to an embodiment of the invention, in the step 1), the Al-Ti-C-CuO mixed powder includes Al powder, Ti powder, C powder and CuO powder, wherein a molar ratio of the Ti powder to the C powder is 1:1.1 to 1.4 (e.g., 1:1, 1:2, 1:3, 1: 4), a weight of the Al powder is 32% to 40% of a total weight of the mixed powder, and a molar ratio of the Al powder to the CuO powder is 1:1.6 to 2 (e.g., 1:1.6, 1:1.7, 1:1.8, 1:1.9, 1: 2).
According to the embodiment of the invention, in the step 1), the addition amount of the Al-Ti-C-CuO mixed powder is 3.5-5.0% of the total weight of the melt.
According to the embodiment of the present invention, step 1) specifically includes the following steps:
1-1) adding a refined aluminum ingot into a crucible, heating to a temperature higher than 650 ℃ until the refined aluminum ingot is completely melted, continuously heating to a temperature higher than 700 ℃, adding an Al-12Si intermediate alloy, stirring for the first time, then continuously heating to a temperature higher than 850 ℃, adding Al-Ti-C-CuO mixed powder, and stirring for the second time;
1-2) cooling the melt obtained in the step 1-1) to 750-770 ℃, adding Al-10La intermediate alloy and Al-5Eu intermediate alloy, and stirring for the third time;
1-3) cooling the melt obtained in the step 1-2) to 725-740 ℃, adding Al-2Sc intermediate alloy and Al-4Zr intermediate alloy, and stirring for the fourth time.
According to the embodiment of the invention, in the step 1-1), the first stirring time is 15 min-25 min, and the second stirring time is 20 min-40 min.
According to the embodiment of the invention, in the step 1-1), after adding the refined aluminum ingot and the Al-12Si intermediate alloy, a primary alloy melt can be obtained in a crucible, the temperature is raised to above 850 ℃, Al-Ti-C-CuO mixed powder is added to carry out high-temperature treatment on the melt, and the coarse bulk Si phase in the melt can be refined into fine bulk.
According to the embodiment of the invention, in the step 1-1), the CuO powder in the Al-Ti-C-CuO mixed powder is used as a catalyst, and after the CuO powder is added, the in-situ reduction reaction of the Al powder, the Ti powder and the C powder can be promoted to generate a large amount of TiC ceramic particles with fine and uniform sizes.
According to the embodiment of the invention, in the step 1-2), the third stirring time is 25-35 min.
According to the embodiment of the invention, in the step 1-2), the Al-10La intermediate alloy and the Al-5Eu intermediate alloy are added to realize the modification effect of the cast aluminum-silicon alloy, specifically, La and Eu elements can modify the Si phase in the alloy melt, the particle size and morphology of the Si phase are improved, and the La and Eu elements can be prevented from being burnt at high temperature when the La and Eu elements are added at the temperature of 750-770 ℃.
According to the embodiment of the invention, in the step 1-3), the fourth stirring time is 20-30 min.
According to the embodiment of the invention, in the step 1-3), the Al-2Sc intermediate alloy and the Al-4Zr intermediate alloy are added to realize the grain refining effect of the cast aluminum-silicon alloy, specifically, Sc and Zr can perform strong refining action on the alloy melt, and the most effective refining action temperature is 725-740 ℃, so that the alloy melt can be subjected to strong refining action after being cooled to 725-740 ℃.
According to the embodiment of the invention, the stirring in the step 1-1) to the step 1-3) is continuously performed by using a steel stirring spoon sprayed with the heat-resistant coating.
According to an embodiment of the invention, the heat-resistant coating comprises the following components in parts by weight: 10-12% of zinc oxide, 12-16% of magnesium oxide, 8-12% of titanium oxide, 4-6% of boric acid, 12-15% of talcum powder and the balance of water.
According to the embodiment of the invention, in the step 2), the deslagging agent comprises the following components in parts by weight: 18-20% of sodium aluminum fluoride, 10-12% of potassium fluoride, 8-10% of sodium fluoride, 12-14% of sodium fluosilicate, 14-16% of potassium fluosilicate, 6-8% of sodium nitrate and the balance of fluorite powder.
According to an embodiment of the invention, in step 2), the slag remover is added in an amount of 0.20% to 0.35%, for example 0.20%, 0.25%, 0.30% or 0.35% of the total weight of the melt.
According to an embodiment of the present invention, in step 2), the degasifier comprises the following components in parts by weight: 6-8% of graphite powder, 28-30% of hexachloroethane, 10-12% of potassium fluosilicate, 12-14% of potassium chloride, 8-10% of sodium fluosilicate, 4-6% of sodium nitrate, 8-10% of potassium nitrate and the balance of sodium chloride.
According to an embodiment of the invention, in step 2), the amount of the degasifier added is 0.15% to 0.30% of the total weight of the melt, for example 0.15%, 0.20%, 0.25% or 0.30%.
According to an embodiment of the present invention, step 2) specifically includes the following steps:
2-1) cooling the melt obtained in the step 1) to 710-725 ℃, and then adding a slag removing agent;
2-2) after the slag removing agent is added, raising the temperature of the melt to 730-745 ℃, and then adding a degassing agent;
optionally, 2-3) skimming the dross on the surface of the melt.
According to the embodiment of the invention, in the step 2-1), the slag removing agent is added into the melt by using a steel bell jar sprayed with the heat-resistant coating, and the bell jar is added at the position 1/3-1/2 of the total height of the melt.
According to the embodiment of the invention, in the step 2-1), when the temperature of adding the slag removing agent into the alloy melt is too high, the slag removing agent is easy to have a strong chemical reaction with the alloy melt to generate a large amount of volatile toxic gas, so that the adding temperature of the slag removing agent is controlled to be 710-725 ℃.
According to the embodiment of the invention, in the step 2-2), a steel bell jar sprayed with a heat-resistant coating is adopted to add the degasifier into the melt, and the bell jar is added at the position 1/2-2/3 of the total height of the melt.
According to the embodiment of the invention, in the step 2-2), when the temperature of the degasifier added into the alloy melt is too high, the degasifier is easy to have a strong chemical reaction with the alloy melt to generate a large amount of volatile toxic gas, so that the adding temperature of the degasifier is controlled to be 730-745 ℃.
According to an embodiment of the present invention, step 3) specifically includes the following steps:
3-1) cooling the melt obtained in the step 2) to 720-730 ℃, and then adding Al-5Ti-B intermediate alloy;
3-2) continuously stirring for 15-20 min by using a steel stirring spoon sprayed with heat-resistant coating after adding, wherein the stirring height of the stirring spoon is 1/2-2/3 of the total height of the melt.
According to the embodiment of the invention, in the step 3-1), the Al-5Ti-B intermediate alloy is added to realize the secondary refining effect of the cast aluminum-silicon alloy. In addition, when the Al-5Ti-B intermediate alloy is added for secondary grain refinement, the Al-5Ti-B intermediate alloy needs to be fully melted to avoid the formation of coarse particle phases in the alloy melt due to insufficient melting, so that the addition temperature is controlled to be 720-730 ℃.
According to the embodiment of the present invention, the step 4) specifically includes the following steps:
4-1) cooling the melt obtained in the step 3) to 685-705 ℃, and then adding pure magnesium ingots and pure lithium ingots;
4-2) introducing gas into the melt after the pure magnesium ingot and the pure lithium ingot are added, performing rotary blowing degassing, and standing the melt for 15-25 min at the temperature of 710-725 ℃ after the rotary blowing degassing.
According to the embodiment of the invention, in the step 4-1), a steel bell jar sprayed with heat-resistant paint is adopted to add pure magnesium ingots (the purity is more than or equal to 99.9%) and pure lithium ingots (the purity is more than or equal to 99.9%) into the melt, and the bell jar is added at 1/3-1/2 of the total height of the melt.
According to the embodiment of the invention, in the step 4-1), Mg and Li are active metals and are easy to burn, so that the melt in the step 3) is cooled to 685-705 ℃, and then pure magnesium ingots and pure lithium ingots are added.
According to the embodiment of the invention, in the step 4-2), the gas in the degassing and standing treatment is mixed gas, and the component and volume ratio of the mixed gas are Cl2 15% -20%, CO12% -15%, and the balance of N2(ii) a The flow rate of the mixed gas is 1.5-2.5 ml/s during rotary blowing, the rotating speed of the rotary rotor is 450-600 r/min, and the rotary blowing time is 10-15 min.
According to the embodiment of the invention, in the step 5), the defects of pinholes and looseness are easily generated when the casting temperature of the alloy melt is too high, the fluidity of the alloy melt is poor when the casting temperature is too low, and the defect of insufficient casting is easily generated, so that the temperature of the alloy melt is adjusted to 705-715 ℃, and the alloy melt is cast in sand molds, metal molds, gypsum molds and investment shell molds to finish casting of castings.
According to the embodiment of the invention, in the step 5), the casting is placed in an electromagnetic induction heating furnace and subjected to electromagnetic induction heating short-time heat treatment.
According to an embodiment of the present invention, in step 5), the electromagnetic induction heating short-time heat treatment includes solution treatment, quenching, pre-aging treatment, and secondary aging treatment. Wherein the heating temperature of the solution treatment is 535-550 ℃, the heating and heat preservation time of the solution treatment is 6-8 h, and the quenching transfer time is less than or equal to 15 s; the heating temperature of the pre-aging treatment is 120-140 ℃, and the heating and heat preservation time of the pre-aging treatment is 1.5-3 h; the heating temperature of the secondary aging treatment is 160-180 ℃, and the heating and heat preservation time of the secondary aging treatment is 4.5-6.0 h.
According to the embodiment of the invention, in the step 5), the electromagnetic induction heating voltage in the electromagnetic induction heating short-time heat treatment is 380V, the induction current is 1.5-3.5A, the induction frequency is 50-60 Hz, and the power is 50-100 kVA.
Compared with the traditional processes of resistance heating or furnace gas combustion heating and the like, the electromagnetic induction heating has remarkable advantages. The electromagnetic induction heating enables the metal in the electromagnetic induction heating to generate heat by itself, the average preheating time is shortened by 2/3 compared with resistance heating, the heat efficiency is up to more than 95%, and the electric energy consumption can be reduced by 30-70%; the electromagnetic induction heating has low batch production cost, can bear high temperature of more than 500 ℃ for a long time, and has reliable service life of more than 5 years. The electromagnetic induction heating temperature control is mainly controlled by a micro-electronic and multi-path intelligent closed-loop system, the operation is reliable and controllable, a control motor can adopt the most advanced industrial PLC control machine board, the aging phenomenon of long-term use is avoided, and the long-term safe and effective operation of equipment is fully ensured; compared with gas combustion or resistance heating, the electromagnetic induction heating greatly improves the operation environment of workers, no waste gas or waste smoke is generated, the control equipment can be manually controlled to implement contact regulation, and the man-machine interaction is greatly improved.
According to an embodiment of the invention, the method comprises the steps of:
(1) smelting: adding a refined aluminum ingot (the purity is more than or equal to 99.99%) into a crucible, heating to above 650 ℃ until the refined aluminum ingot is completely melted, continuously heating to above 700 ℃, adding an Al-12Si intermediate alloy, continuously stirring for 15-25 min by using a steel stirring spoon coated with a heat-resistant coating, then continuously heating to above 850 ℃, adding Al-Ti-C-CuO mixed powder into the melt by using a steel bell jar coated with the heat-resistant coating, and continuously stirring for 20-40 min after adding;
(2) modification: cooling the melt prepared in the step (1) to 750-770 ℃, adding an Al-10La intermediate alloy and an Al-5Eu intermediate alloy into the melt by using a steel stirring spoon coated with a heat-resistant coating, and continuously stirring for 25-35 min after adding;
(3) grain refinement: cooling the melt prepared in the step (2) to 725-740 ℃, adding an Al-2Sc intermediate alloy and an Al-4Zr intermediate alloy into the melt by using a steel stirring spoon sprayed with a heat-resistant coating, and continuously stirring for 20-30 min after adding;
(4) degassing and deslagging: cooling the melt prepared in the step (3) to 710-725 ℃, adding a deslagging agent into the melt by using a steel bell jar sprayed with a heat-resistant coating, adding the bell jar at a position with the height of 1/3-1/2 of the total height of the melt, raising the temperature of the melt to 730-745 ℃ after the deslagging agent is added, adding a degassing agent into the melt by using the steel bell jar sprayed with the heat-resistant coating, adding the bell jar at a position with the height of 1/2-2/3 of the total height of the melt, and skimming scum on the surface of the melt by using a steel stirring spoon sprayed with the heat-resistant coating after the degassing agent is added;
(5) secondary refining: cooling the melt prepared in the step (4) to 720-730 ℃, adding Ti element into the melt in the form of Al-5Ti-B intermediate alloy wire, and continuously stirring for 15-20 min by using a steel stirring spoon sprayed with heat-resistant paint, wherein the stirring height of the stirring spoon is 1/2-2/3 of the total height of the melt;
(6) blowing degassing and standing treatment: cooling the melt prepared in the step (5) to 685-705 ℃, adding a pure magnesium ingot (the purity is more than or equal to 99.9%) and a pure lithium ingot (the purity is more than or equal to 99.9%) into the melt by using a bell jar sprayed with a heat-resistant coating, adding 1/3-1/2 parts with the height of the total melt by using the bell jar, introducing gas into the melt after the pure magnesium ingot and the pure lithium ingot are added, carrying out rotary blowing degassing, and standing the melt for 15-25 min at the temperature of 710-725 ℃ after the rotary blowing degassing;
(7) casting: adjusting the temperature of the melt to 705-715 ℃, and casting the alloy melt in a sand mold, a metal mold, a gypsum mold or a fired mold shell mold to finish casting of the casting;
(8) electromagnetic induction heating short-time heat treatment: placing the casting in an electromagnetic induction heating furnace, wherein the solid solution heating temperature is 535-550 ℃, the solid solution heating heat preservation time is 6-8 h, and the quenching transfer time is less than or equal to 15 s; the pre-aging heating temperature is 120-140 ℃, and the pre-aging heating heat preservation time is 1.5-3 h; the secondary aging heating temperature is 160-180 ℃, and the secondary aging heating heat preservation time is 4.5-6.0 h.
The invention has the beneficial effects that:
compared with the traditional ZL101 and ZL114 cast aluminum-silicon alloy materials, the high-strength and high-toughness cast aluminum-silicon alloy provided by the invention has the advantages that Al-Ti-C-CuO mixed powder is added in the preparation process of the high-strength and high-toughness cast aluminum-silicon alloy, the reaction shown as the formula-1 is carried out, and a large amount of TiC ceramic particles with small and uniform sizes are generated in a melt through the reaction; the eutectic silicon phase is fully and effectively modified by virtue of Eu and La rare earth elements, the morphology of the silicon phase can be changed from a plate shape and a needle shape into a spherical shape, the stress concentration degree of the tip of the silicon phase is greatly reduced, and the plasticity and toughness of the material are improved. Through grain refinement, secondary refinement, blowing degassing and standing treatment, a large amount of Al is formed in the melt3Sc、Al3Zr heterogeneous nucleation particles, [ H ] in the melt]Ion content and Al2O3The number of oxide films is effectively reduced. After adding trace Li element, the alloy can be further meltedIn the body [ H]Ion formation of LiH and Li3AlH6The compound (shown as the formula-2) can improve the purity of the melt. The short-time rapid high-efficiency heat treatment of the prepared cast aluminum-silicon alloy can be realized by combining the electromagnetic induction heating short-time heat treatment process after the melt is cast, a large amount of micro TiC ceramic particles are separated out from the grain boundary in the material crystal by refining the crystal grains of the alloy material and improving the appearance, the size and the orientation distribution of the silicon phase, the high-strength and high-toughness preparation of the alloy material is realized, the short-period low-cost casting of the precision aluminum alloy casting with the complex structure of military equipment can be realized, and the economic benefit is obvious.
Figure DEST_PATH_IMAGE002A
Drawings
Fig. 1 is the as-cast metallographic OM test result of the cast aluminum-silicon alloy of example 1.
FIG. 2 shows the results of mechanical properties of cast Al-Si alloy in example 2 after short-time heat treatment.
FIG. 3 is TEM morphology test result of TiC microstructure of cast Al-Si alloy in example 3.
FIG. 4 is a schematic view of an electromagnetic induction heating short-time heat treatment structure of a metal shell casting of the tail section in embodiment 4;
FIG. 4 is a drawing of a missile shell casting; secondly, heat treatment of the insulation box for a short time; thirdly, a heat conducting rod of the missile shell casting; heat insulation sealing plug; fifthly, spraying a quenching spray head; sixthly, the electromagnetic induction heater.
Detailed Description
The present invention will be described in further detail with reference to specific examples. It is to be understood that the following examples are only illustrative and explanatory of the present invention and should not be construed as limiting the scope of the present invention. All the technologies realized based on the above-mentioned contents of the present invention are covered in the protection scope of the present invention.
The experimental methods used in the following examples are all conventional methods unless otherwise specified; reagents, materials and the like used in the following examples are commercially available unless otherwise specified.
Example 1:
a preparation method and a heat treatment method of high-strength cast aluminum-silicon alloy are disclosed, wherein the high-strength cast aluminum-silicon alloy comprises the following components in parts by weight: 7% of Si, 0.6% of Mg, 0.18% of Sc, 0.20% of Zr, 0.12% of Eu, 0.15% of La, 0.14% of Ti, 0.04% of Li, 0.02% of C and the balance of aluminum; the preparation method comprises the following steps:
(1) smelting: adding refined aluminum ingots (with the purity of 99.99%) into a crucible, heating to above 650 ℃ until the refined aluminum ingots are completely melted, continuing to heat to above 700 ℃, adding Al-12Si master alloy, continuously stirring for 15min by using a steel stirring spoon coated with heat-resistant paint, then continuing to heat to above 850 ℃, adding in-situ chemical reaction powder into the melt by using a steel bell jar coated with heat-resistant paint, and continuously stirring for 20min after adding;
(2) modification: cooling the melt prepared in the step (1) to 750 ℃, adding Al-10La intermediate alloy and Al-5Eu intermediate alloy into the melt by using a steel stirring spoon coated with heat-resistant coating, and continuously stirring for 25min after adding;
(3) grain refinement: cooling the melt prepared in the step (2) to 725 ℃, adding an Al-2Sc intermediate alloy and an Al-4Zr intermediate alloy into the melt by using a steel stirring spoon sprayed with a heat-resistant coating, and continuously stirring for 20min after adding;
(4) degassing and deslagging: cooling the melt prepared in the step (3) to 710 ℃, adding a deslagging agent into the melt by using a steel bell jar sprayed with a heat-resistant coating, adding the bell jar at 1/3, which is the total height of the melt, raising the temperature of the melt to 730 ℃ after the deslagging agent is added, adding a degassing agent into the melt by using the steel bell jar sprayed with the heat-resistant coating, adding the bell jar at 1/2, which is the total height of the melt, and skimming dross on the surface of the melt by using a steel stirring spoon sprayed with the heat-resistant coating after the degassing agent is added;
(5) secondary refining: cooling the melt prepared in the step (4) to 720 ℃, adding Ti element into the melt in the form of Al-5Ti-B intermediate alloy of wire material, and continuously stirring for 15min by using a steel stirring spoon sprayed with heat-resistant coating, wherein the stirring height of the stirring spoon is 1/2 of the total height of the melt;
(6) blowing degassing and standing treatment: cooling the melt prepared in the step (5) to 685 ℃, adding a pure magnesium ingot (with the purity of 99.9%) and a pure lithium ingot (with the purity of 99.9%) into the melt by using a bell jar sprayed with a heat-resistant coating, adding 1/3 parts with the height of the total height of the melt by using the bell jar, introducing gas into the melt after the pure magnesium ingot and the pure lithium ingot are added, carrying out rotary blowing degassing, and controlling the temperature of the melt at 710 ℃ for standing treatment for 15min after the rotary blowing degassing;
(7) casting: adjusting the temperature of the melt to 705 ℃, and casting the alloy melt in the investment shell mold to finish casting of the casting;
(8) electromagnetic induction heating short-time heat treatment: placing the casting in an electromagnetic induction heating furnace, wherein the solid solution heating temperature is 535 ℃, the solid solution heating heat preservation time is 6h, and the quenching transfer time is 15 s; the pre-aging heating temperature is 120 ℃, and the pre-aging heating heat preservation time is 1.5 h; the secondary aging heating temperature is 160 ℃, and the secondary aging heating heat preservation time is 4.5 h.
In the smelting in the step (1), the in-situ chemical reaction powder is Al-Ti-C-CuO mixed powder, wherein the molar ratio of Ti powder to C powder is 1:1.1, Al powder accounts for 32% of the total weight of the mixed powder, the molar ratio of Al powder to CuO powder is 1:1.6, and the adding amount of the Al-Ti-C-CuO mixed powder accounts for 3.5% of the total weight of the melt.
The heat-resistant coating in the modification in the step (2) comprises the following components in percentage by weight: 10% of zinc oxide, 12% of magnesium oxide, 8% of titanium oxide, 4% of boric acid, 12% of talcum powder and the balance of water.
The deslagging agent in the degassing and deslagging step (4) comprises the following components in percentage by weight: 18% of sodium aluminum fluoride, 10% of potassium fluoride, 8% of sodium fluoride, 12% of sodium fluosilicate, 14% of potassium fluosilicate, 6% of sodium nitrate and the balance of fluorite powder; the addition amount of the slag removing agent is 0.20 percent of the total weight of the fusant.
The components of the degasifier in the degassing and deslagging step (4) and the weight ratio thereof are as follows: 6% of graphite powder, 28% of hexachloroethane, 10% of potassium fluosilicate, 12% of potassium chloride, 8% of sodium fluosilicate, 4% of sodium nitrate, 8% of potassium nitrate and the balance of sodium chloride; the addition amount of the degasifier is 0.15 percent of the total weight of the melt.
The blowing degassing and standing treatment in step (6)The gas is mixed gas, and the components and the volume ratio of the mixed gas are Cl215%, CO12%, the balance being N2(ii) a The flow rate of the mixed gas is 1.5ml/s during rotary blowing, the rotating speed of the rotary rotor is 450r/min, and the rotary blowing time is 10 min.
And (8) in the electromagnetic induction heating short-time heat treatment, the electromagnetic induction heating voltage is 380V, the induction current is 1.5A, the induction frequency is 50Hz, and the power is 50 kVA.
After the prepared cast aluminum-silicon alloy is subjected to electromagnetic induction heating short-time heat treatment in the step (8), the tensile strength is 340MPa, the yield strength is 280MPa, the elongation is 6%, and the Brinell hardness is 120 HBS.
FIG. 1 shows the OM test result of the as-cast metallographic structure of the cast Al-Si alloy with high strength and toughness prepared in example 1. As can be seen from FIG. 1, the high-toughness cast aluminum-silicon alloy prepared by the invention has fine crystal grains, the average crystal grain size of the primary alpha-Al matrix is about 82 μm and is far lower than the average crystal grain size (about 160 μm) of the cast primary alpha-Al matrix of the traditional cast aluminum-silicon alloy, and the eutectic Si phase in the grain boundary area has no coarse blocky or plate-like appearance and is distributed in a fine polygonal shape.
Example 2:
a preparation method and a heat treatment method of high-strength cast aluminum-silicon alloy are disclosed, wherein the high-strength cast aluminum-silicon alloy comprises the following components in parts by weight: 9% of Si, 0.9% of Mg, 0.30% of Sc, 0.36% of Zr, 0.20% of Eu, 0.25% of La, 0.22% of Ti, 0.08% of Li, 0.06% of C and the balance of aluminum; the preparation method comprises the following steps:
(1) smelting: adding refined aluminum ingots (with the purity of 99.99 percent) into a crucible, heating to above 650 ℃ until the refined aluminum ingots are completely melted, continuing to heat to above 700 ℃, adding Al-12Si master alloy, continuously stirring for 25min by using a steel stirring spoon coated with heat-resistant paint, then continuing to heat to above 850 ℃, adding in-situ chemical reaction powder into the melt by using a steel bell jar coated with heat-resistant paint, and continuously stirring for 40min after adding;
(2) modification: cooling the melt prepared in the step (1) to 770 ℃, adding the Al-10La intermediate alloy and the Al-5Eu intermediate alloy into the melt by using a steel stirring spoon coated with heat-resistant coating, and continuously stirring for 35min after adding;
(3) grain refinement: cooling the melt prepared in the step (2) to 740 ℃, adding an Al-2Sc intermediate alloy and an Al-4Zr intermediate alloy into the melt by using a steel stirring spoon coated with a heat-resistant coating, and continuously stirring for 30min after adding;
(4) degassing and deslagging: cooling the melt prepared in the step (3) to 725 ℃, adding a deslagging agent into the melt by using a steel bell jar sprayed with a heat-resistant coating, adding the bell jar at 1/2 with the height of the total height of the melt, raising the temperature of the melt to 745 ℃ after the deslagging agent is added, adding a degassing agent into the melt by using the steel bell jar sprayed with the heat-resistant coating, adding the bell jar at 2/3 with the height of the total height of the melt, and skimming dross on the surface of the melt by using a steel stirring spoon sprayed with the heat-resistant coating after the degassing agent is added;
(5) secondary refining: cooling the melt prepared in the step (4) to 730 ℃, adding Ti element into the melt in the form of Al-5Ti-B intermediate alloy of wire material, and continuously stirring for 20min by using a steel stirring spoon sprayed with heat-resistant coating, wherein the stirring height of the stirring spoon is 2/3 of the total height of the melt;
(6) blowing degassing and standing treatment: cooling the melt prepared in the step (5) to 705 ℃, adding a pure magnesium ingot (with the purity of 99.94%) and a pure lithium ingot (with the purity of 99.96%) into the melt by using a bell jar sprayed with a heat-resistant coating, adding the bell jar into a position 1/2 with the height of the total height of the melt, introducing gas into the melt after adding the pure magnesium ingot and the pure lithium ingot to carry out rotary blowing degassing, and carrying out rotary blowing degassing on the melt, and then controlling the temperature of the melt at 725 ℃ for standing treatment for 25 min;
(7) casting: adjusting the temperature of the melt to 715 ℃, and casting the alloy melt in a metal mold to finish casting of a casting;
(8) electromagnetic induction heating short-time heat treatment: placing the casting in an electromagnetic induction heating furnace, wherein the solid solution heating temperature is 550 ℃, the solid solution heating heat preservation time is 8h, and the quenching transfer time is 12 s; the pre-aging heating temperature is 140 ℃, and the pre-aging heating heat preservation time is 3 h; the secondary aging heating temperature is 180 ℃, and the secondary aging heating heat preservation time is 6.0 h.
The in-situ chemical reaction powder in the smelting in the step (1) is Al-Ti-C-CuO mixed powder, wherein the molar ratio of Ti powder to C powder is 1:1.4, the Al powder accounts for 40% of the total weight of the mixed powder, the molar ratio of Al powder to CuO powder is 1:2.0, and the adding amount of the Al-Ti-C-CuO mixed powder accounts for 5.0% of the total weight of the melt.
The heat-resistant coating in the modification in the step (2) comprises the following components in percentage by weight: 12% of zinc oxide, 16% of magnesium oxide, 12% of titanium oxide, 6% of boric acid, 15% of talcum powder and the balance of water.
The deslagging agent in the degassing and deslagging step (4) comprises the following components in percentage by weight: 20% of sodium aluminum fluoride, 12% of potassium fluoride, 10% of sodium fluoride, 14% of sodium fluosilicate, 16% of potassium fluosilicate, 8% of sodium nitrate and the balance of fluorite powder; the addition amount of the slag remover is 0.35 percent of the total weight of the fusant.
The components of the degasifier in the degassing and deslagging step (4) and the weight ratio thereof are as follows: 8% of graphite powder, 30% of hexachloroethane, 12% of potassium fluosilicate, 14% of potassium chloride, 10% of sodium fluosilicate, 6% of sodium nitrate, 10% of potassium nitrate and the balance of sodium chloride; the addition amount of the degasifier is 0.30 percent of the total weight of the melt.
The gas in the blowing degassing and standing treatment in the step (6) is mixed gas, and the components and the volume ratio of the mixed gas are Cl 220%, CO15%, the balance being N2(ii) a The flow rate of the mixed gas is 2.5ml/s during rotary blowing, the rotating speed of the rotary rotor is 600r/min, and the rotary blowing time is 15 min.
And (3) in the step (8) of electromagnetic induction heating short-time heat treatment, the electromagnetic induction heating voltage is 380V, the induction current is 3.5A, the induction frequency is 60Hz, and the power is 100 kVA.
Fig. 2 shows the mechanical property test results of the cast aluminum-silicon alloy prepared in example 2 after being subjected to electromagnetic induction heating short-time heat treatment. As can be seen from FIG. 2, the tensile strength of the cast aluminum-silicon alloy is 368 MPa-377 MPa, the yield strength of the cast aluminum-silicon alloy is 306 MPa-318 MPa, the elongation of the cast aluminum-silicon alloy is 7.4% -8.6%, and the Brinell hardness of the cast aluminum-silicon alloy is above 130 HBS.
Example 3:
a preparation method and a heat treatment method of high-strength cast aluminum-silicon alloy are disclosed, wherein the high-strength cast aluminum-silicon alloy comprises the following components in parts by weight: 8% of Si, 0.75% of Mg, 0.24% of Sc, 0.28% of Zr, 0.16% of Eu, 0.20% of La, 0.18% of Ti, 0.06% of Li, 0.04% of C and the balance of aluminum; the preparation method comprises the following steps:
(1) smelting: adding refined aluminum ingots (with the purity of 99.99 percent) into a crucible, heating to above 650 ℃ until the refined aluminum ingots are completely melted, continuing to heat to above 700 ℃, adding Al-12Si intermediate alloy, continuously stirring for 20min by using a steel stirring spoon coated with heat-resistant paint, then continuing to heat to above 850 ℃, adding in-situ chemical reaction powder into the melt by using a steel bell jar coated with heat-resistant paint, and continuously stirring for 30min after adding;
(2) modification: cooling the melt prepared in the step (1) to 760 ℃, adding Al-10La intermediate alloy and Al-5Eu intermediate alloy into the melt by using a steel stirring spoon coated with heat-resistant coating, and continuously stirring for 30min after adding;
(3) grain refinement: cooling the melt prepared in the step (2) to 732 ℃, adding an Al-2Sc intermediate alloy and an Al-4Zr intermediate alloy into the melt by using a steel stirring spoon sprayed with a heat-resistant coating, and continuously stirring for 25min after adding;
(4) degassing and deslagging: cooling the melt prepared in the step (3) to 718 ℃, adding a deslagging agent into the melt by using a steel bell jar sprayed with a heat-resistant coating, adding the bell jar at 1/3, which is the total height of the melt, raising the temperature of the melt to 738 ℃ after the deslagging agent is added, adding a degassing agent into the melt by using the steel bell jar sprayed with the heat-resistant coating, adding the bell jar at 1/2, which is the total height of the melt, and skimming dross on the surface of the melt by using a steel stirring spoon sprayed with the heat-resistant coating after the degassing agent is added;
(5) secondary refining: cooling the melt prepared in the step (4) to 725 ℃, adding Ti element into the melt in the form of Al-5Ti-B intermediate alloy of wire material, and continuously stirring for 18min by using a steel stirring spoon sprayed with heat-resistant coating, wherein the stirring height of the stirring spoon is 2/3 of the total height of the melt;
(6) blowing degassing and standing treatment: cooling the melt prepared in the step (5) to 695 ℃, adding a pure magnesium ingot (with the purity of 99.9%) and a pure lithium ingot (with the purity of 99.9%) into the melt by using a bell jar sprayed with a heat-resistant coating, adding 1/2 parts with the height of the total height of the melt by using the bell jar, introducing gas into the melt after the pure magnesium ingot and the pure lithium ingot are added, carrying out rotary blowing degassing, and standing the melt for 20min at the temperature of 718 ℃ after the rotary blowing degassing;
(7) casting: adjusting the temperature of the melt to 710 ℃, and casting the alloy melt in the gypsum mold to finish casting of the casting;
(8) electromagnetic induction heating short-time heat treatment: placing the casting in an electromagnetic induction heating furnace, wherein the solid solution heating temperature is 542 ℃, the solid solution heating heat preservation time is 7h, and the quenching transfer time is 10 s; the pre-aging heating temperature is 130 ℃, and the pre-aging heating heat preservation time is 2.2 h; the secondary aging heating temperature is 170 ℃, and the secondary aging heating heat preservation time is 5 h.
The in-situ chemical reaction powder in the smelting in the step (1) is Al-Ti-C-CuO mixed powder, wherein the molar ratio of Ti powder to C powder is 1:1.2, the Al powder accounts for 34% of the total weight of the mixed powder, the molar ratio of Al powder to CuO powder is 1:1.7, and the adding amount of the Al-Ti-C-CuO mixed powder accounts for 4.3% of the total weight of the melt.
The heat-resistant coating in the modification in the step (2) comprises the following components in percentage by weight: 11% of zinc oxide, 14% of magnesium oxide, 10% of titanium oxide, 5% of boric acid, 13.5% of talcum powder and the balance of water.
The deslagging agent in the degassing and deslagging step (4) comprises the following components in percentage by weight: 19% of sodium aluminum fluoride, 11% of potassium fluoride, 9% of sodium fluoride, 13% of sodium fluosilicate, 15% of potassium fluosilicate, 7% of sodium nitrate and the balance of fluorite powder; the addition amount of the slag remover is 0.25 percent of the total weight of the fusant.
The components of the degasifier in the degassing and deslagging step (4) and the weight ratio thereof are as follows: 7% of graphite powder, 29% of hexachloroethane, 11% of potassium fluosilicate, 13% of potassium chloride, 9% of sodium fluosilicate, 5% of sodium nitrate, 9% of potassium nitrate and the balance of sodium chloride; the addition amount of the degasifier is 0.22 percent of the total weight of the melt.
The gas in the blowing degassing and standing treatment in the step (6) is mixed gas, and the components and the volume ratio of the mixed gas are Cl217.5%，CO13.5%, the balance being N2(ii) a The flow rate of the mixed gas is 2.0ml/s during rotary blowing, the rotating speed of the rotary rotor is 525r/min, and the rotary blowing time is 12.5 min.
And (3) in the step (8) of electromagnetic induction heating short-time heat treatment, the electromagnetic induction heating voltage is 380V, the induction current is 2A, the induction frequency is 55Hz, and the power is 75 kVA.
After the prepared cast aluminum-silicon alloy is subjected to electromagnetic induction heating short-time heat treatment in the step (8), the tensile strength is 360MPa, the yield strength is 300MPa, the elongation is 8%, and the Brinell hardness is 130 HBS.
Fig. 3 shows TEM morphology test results of TiC particles in the microstructure of the high-toughness cast aluminum-silicon alloy prepared in example 3. It can be seen from fig. 3 that TiC particles are formed in situ in the aluminum-silicon alloy.
Example 4:
a preparation method and a heat treatment method of high-strength cast aluminum-silicon alloy are disclosed, wherein the high-strength cast aluminum-silicon alloy comprises the following components in parts by weight: 8.5% of Si, 0.8% of Mg, 0.25% of Sc, 0.28% of Zr, 0.18% of Eu, 0.22% of La, 0.20% of Ti, 0.07% of Li, 0.05% of C and the balance of aluminum; the preparation method comprises the following steps:
(1) smelting: adding refined aluminum ingots (with the purity of 99.99%) into a crucible, heating to above 650 ℃ until the refined aluminum ingots are completely melted, continuously heating to above 700 ℃, adding Al-12Si master alloy, continuously stirring for 22min by using a steel stirring spoon coated with heat-resistant paint, then continuously heating to above 850 ℃, adding in-situ chemical reaction powder into the melt by using a steel bell jar coated with heat-resistant paint, and continuously stirring for 35min after adding;
(2) modification: cooling the melt prepared in the step (1) to 765 ℃, adding the Al-10La intermediate alloy and the Al-5Eu intermediate alloy into the melt by using a steel stirring spoon sprayed with heat-resistant paint, and continuously stirring for 32min after adding;
(3) grain refinement: cooling the melt prepared in the step (2) to 735 ℃, adding an Al-2Sc intermediate alloy and an Al-4Zr intermediate alloy into the melt by using a steel stirring spoon coated with a heat-resistant coating, and continuously stirring for 28min after adding;
(4) degassing and deslagging: cooling the melt prepared in the step (3) to 722 ℃, adding a deslagging agent into the melt by using a steel bell jar sprayed with a heat-resistant coating, adding the bell jar at 1/2, which is the total height of the melt, raising the temperature of the melt to 742 ℃ after the deslagging agent is added, adding a degassing agent into the melt by using the steel bell jar sprayed with the heat-resistant coating, adding the bell jar at 2/3, which is the total height of the melt, and skimming dross on the surface of the melt by using a steel stirring spoon sprayed with the heat-resistant coating after the degassing agent is added;
(5) secondary refining: cooling the melt prepared in the step (4) to 728 ℃, adding Ti element into the melt in the form of Al-5Ti-B intermediate alloy of wire material, and continuously stirring for 18min by using a steel stirring spoon sprayed with heat-resistant coating, wherein the stirring height of the stirring spoon is 2/3 of the total height of the melt;
(6) blowing degassing and standing treatment: cooling the melt prepared in the step (5) to 702 ℃, adding a pure magnesium ingot (with the purity of 99.99%) and a pure lithium ingot (with the purity of 99.98%) into the melt by using a bell jar sprayed with a heat-resistant coating, adding the bell jar into a position 1/2 with the height of the total height of the melt, introducing gas into the melt after the pure magnesium ingot and the pure lithium ingot are added, carrying out rotary blowing degassing, and controlling the temperature of the melt at 722 ℃ for standing treatment for 24min after the rotary blowing degassing;
(7) casting: adjusting the temperature of the melt to 712 ℃, and casting the alloy melt in the sand mold to finish casting of the casting;
(8) electromagnetic induction heating short-time heat treatment: placing the casting in an electromagnetic induction heating furnace, wherein the solid solution heating temperature is 545 ℃, the solid solution heating heat preservation time is 7.5h, and the quenching transfer time is 8 s; the pre-aging heating temperature is 135 ℃, and the pre-aging heating heat preservation time is 2.5 h; the temperature of the secondary aging heating is 175 ℃, and the time of the secondary aging heating and heat preservation is 5.5 h.
The in-situ chemical reaction powder in the smelting in the step (1) is Al-Ti-C-CuO mixed powder, wherein the molar ratio of Ti powder to C powder is 1:1.3, the Al powder accounts for 38% of the total weight of the mixed powder, the molar ratio of Al powder to CuO powder is 1:1.9, and the adding amount of the Al-Ti-C-CuO mixed powder accounts for 4.8% of the total weight of the melt.
The heat-resistant coating in the modification in the step (2) comprises the following components in percentage by weight: 11.5% of zinc oxide, 15.5% of magnesium oxide, 11.2% of titanium oxide, 5.4% of boric acid, 14.5% of talcum powder and the balance of water.
The deslagging agent in the degassing and deslagging step (4) comprises the following components in percentage by weight: 19.5% of sodium aluminum fluoride, 11.4% of potassium fluoride, 9.6% of sodium fluoride, 13.2% of sodium fluosilicate, 15.6% of potassium fluosilicate, 7.6% of sodium nitrate and the balance of fluorite powder; the addition amount of the deslagging agent is 0.30 percent of the total weight of the fusant.
The components of the degasifier in the degassing and deslagging step (4) and the weight ratio thereof are as follows: 7.2% of graphite powder, 29.5% of hexachloroethane, 11.6% of potassium fluosilicate, 13.6% of potassium chloride, 9.4% of sodium fluosilicate, 5.8% of sodium nitrate, 9.2% of potassium nitrate and the balance of sodium chloride; the addition amount of the degasifier is 0.26 percent of the total weight of the melt.
The gas in the blowing degassing and standing treatment in the step (6) is mixed gas, and the components and the volume ratio of the mixed gas are Cl219%, CO14.5%, and the balance N2(ii) a The flow rate of the mixed gas is 2.4ml/s during rotary blowing, the rotating speed of the rotary rotor is 560r/min, and the rotary blowing time is 14 min.
And (3) in the step (8) of electromagnetic induction heating short-time heat treatment, the electromagnetic induction heating voltage is 380V, the induction current is 3.2A, the induction frequency is 58Hz, and the power is 90 kVA.
After the prepared cast aluminum-silicon alloy is subjected to electromagnetic induction heating short-time heat treatment in the step (8), the tensile strength is 365MPa, the yield strength is 312MPa, the elongation is 8.6%, and the Brinell hardness is 132 HBS.
Fig. 4 is a schematic structural view of electromagnetic induction heating short-time heat treatment of a tail section metal shell casting prepared in example 4.
The embodiments of the present invention have been described above. However, the present invention is not limited to the above embodiment. Any modification, equivalent replacement, or improvement made without departing from the spirit and principle of the present invention shall fall within the protection scope of the present invention.

Claims (10)

1. A cast aluminum-silicon alloy, characterized in that it comprises the following components in weight percent:
7-9% of Si, 0.6-0.9% of Mg, 0.18-0.30% of Sc, 0.20-0.36% of Zr, 0.12-0.20% of Eu, 0.15-0.25% of La, 0.14-0.22% of Ti, 0.04-0.08% of Li, 0.02-0.06% of C and the balance of Al and inevitable impurities.
2. The cast aluminum-silicon alloy according to claim 1, characterized in that it comprises the following composition in weight percent: b, 0-0.02%;
and/or, the cast aluminum-silicon alloy comprises the following components in percentage by weight: 0-0.02% of Cu.
3. The cast aluminum-silicon alloy according to claim 1 or 2, wherein the cast aluminum-silicon alloy has a tensile strength of 340 to 380 MPa;
and/or the yield strength of the cast aluminum-silicon alloy is 280 MPa-320 MPa;
and/or the elongation of the cast aluminum-silicon alloy is 6-10%;
and/or the Brinell hardness of the cast aluminum-silicon alloy is 120 HBS-140 HBS.
4. A method of producing a cast aluminium silicon alloy according to any one of claims 1 to 3, the method comprising the steps of:
1) mixing and smelting the refined aluminum ingot, Al-12Si intermediate alloy, Al-10La intermediate alloy, Al-5Eu intermediate alloy, Al-2Sc intermediate alloy, Al-4Zr intermediate alloy and Al-Ti-C-CuO mixed powder;
2) adding a deslagging agent and a degassing agent into the melt obtained in the step 1), and degassing and deslagging;
3) adding Al-5Ti-B intermediate alloy into the melt obtained in the step 2) for secondary refining treatment;
4) adding a pure magnesium ingot and a pure lithium ingot into the melt obtained in the step 3), and then carrying out blowing degassing and standing treatment;
5) casting the melt obtained in the step 4), and then carrying out electromagnetic induction heating short-time heat treatment to prepare the cast aluminum-silicon alloy.
5. The preparation method according to claim 4, wherein in the step 1), the Al-Ti-C-CuO mixed powder comprises Al powder, Ti powder, C powder and CuO powder, wherein the molar ratio of the Ti powder to the C powder is 1: 1.1-1.4, the weight of the Al powder accounts for 32-40% of the total weight of the mixed powder, and the molar ratio of the Al powder to the CuO powder is 1: 1.6-2;
and/or in the step 1), the adding amount of the Al-Ti-C-CuO mixed powder accounts for 3.5-5.0% of the total weight of the melt.
6. The preparation method according to claim 4, wherein the step 1) specifically comprises the following steps:
1-1) adding refined aluminum cast ingots into a crucible, heating to a temperature of above 650 ℃ until the refined aluminum cast ingots are completely melted, continuously heating to a temperature of above 700 ℃, adding Al-12Si intermediate alloy, stirring for the first time, then continuously heating to a temperature of above 850 ℃, adding Al-Ti-C-CuO mixed powder, and stirring for the second time;
1-2) cooling the melt obtained in the step 1-1) to 750-770 ℃, adding Al-10La intermediate alloy and Al-5Eu intermediate alloy, and stirring for the third time;
1-3) cooling the melt obtained in the step 1-2) to 725-740 ℃, adding Al-2Sc intermediate alloy and Al-4Zr intermediate alloy, and stirring for the fourth time.
7. The preparation method according to claim 4, wherein in the step 2), the deslagging agent comprises the following components in parts by weight: 18-20% of sodium aluminum fluoride, 10-12% of potassium fluoride, 8-10% of sodium fluoride, 12-14% of sodium fluosilicate, 14-16% of potassium fluosilicate, 6-8% of sodium nitrate and the balance of fluorite powder;
and/or, in the step 2), the addition amount of the deslagging agent is 0.20-0.35% of the total weight of the melt;
and/or, in the step 2), the degasifier comprises the following components in parts by weight: 6-8% of graphite powder, 28-30% of hexachloroethane, 10-12% of potassium fluosilicate, 12-14% of potassium chloride, 8-10% of sodium fluosilicate, 4-6% of sodium nitrate, 8-10% of potassium nitrate and the balance of sodium chloride;
and/or in the step 2), the addition amount of the degasifier is 0.15-0.30% of the total weight of the melt.
8. The preparation method according to claim 4, wherein the step 2) specifically comprises the following steps:
2-1) cooling the melt obtained in the step 1) to 710-725 ℃, and then adding a deslagging agent;
2-2) after the slag removing agent is added, raising the temperature of the melt to 730-745 ℃, and then adding a degassing agent;
optionally, 2-3) skimming the scum on the surface of the melt;
and/or, in the step 3), the method specifically comprises the following steps:
3-1) cooling the melt obtained in the step 2) to 720-730 ℃, and then adding Al-5Ti-B intermediate alloy;
3-2) continuously stirring for 15-20 min by using a steel stirring spoon sprayed with heat-resistant coating after adding, wherein the stirring height of the stirring spoon is 1/2-2/3 of the total height of the melt;
and/or, in the step 4), the method specifically comprises the following steps:
4-1) cooling the melt obtained in the step 3) to 685-705 ℃, and then adding pure magnesium ingots and pure lithium ingots;
4-2) introducing gas into the melt after the pure magnesium ingot and the pure lithium ingot are added, performing rotary blowing degassing, and standing the melt for 15-25 min at the temperature of 710-725 ℃ after the rotary blowing degassing.
9. The method for preparing the alloy material according to claim 4, wherein in the step 5), the electromagnetic induction heating short-time heat treatment comprises solution treatment, quenching, pre-aging treatment and secondary aging treatment; wherein the heating temperature of the solution treatment is 535-550 ℃, the heating and heat preservation time of the solution treatment is 6-8 h, and the quenching transfer time is less than or equal to 15 s; the heating temperature of the pre-aging treatment is 120-140 ℃, and the heating and heat preservation time of the pre-aging treatment is 1.5-3 h; the heating temperature of the secondary aging treatment is 160-180 ℃, and the heating and heat preservation time of the secondary aging treatment is 4.5-6.0 h;
and/or in the step 5), the electromagnetic induction heating voltage is 380V, the induction current is 1.5-3.5A, the induction frequency is 50-60 Hz, and the power is 50-100 kVA in the electromagnetic induction heating short-time heat treatment.
10. The method for preparing according to claim 4, characterized in that it comprises the steps of:
(1) smelting: adding refined aluminum ingots into a crucible, heating to a temperature higher than 650 ℃ until the refined aluminum ingots are completely melted, continuously heating to a temperature higher than 700 ℃, adding an Al-12Si intermediate alloy, continuously stirring for 15-25 min by using a steel stirring spoon coated with a heat-resistant coating, then continuously heating to a temperature higher than 850 ℃, adding Al-Ti-C-CuO mixed powder into the melt by using a steel bell jar coated with the heat-resistant coating, and continuously stirring for 20-40 min after adding;
(2) modification: cooling the melt prepared in the step (1) to 750-770 ℃, adding an Al-10La intermediate alloy and an Al-5Eu intermediate alloy into the melt by using a steel stirring spoon coated with a heat-resistant coating, and continuously stirring for 25-35 min after adding;
(3) grain refinement: cooling the melt prepared in the step (2) to 725-740 ℃, adding an Al-2Sc intermediate alloy and an Al-4Zr intermediate alloy into the melt by using a steel stirring spoon sprayed with a heat-resistant coating, and continuously stirring for 20-30 min after adding;
(4) degassing and deslagging: cooling the melt prepared in the step (3) to 710-725 ℃, adding a deslagging agent into the melt by using a steel bell jar sprayed with a heat-resistant coating, adding the bell jar at a position with the height of 1/3-1/2 of the total height of the melt, raising the temperature of the melt to 730-745 ℃ after the deslagging agent is added, adding a degassing agent into the melt by using the steel bell jar sprayed with the heat-resistant coating, adding the bell jar at a position with the height of 1/2-2/3 of the total height of the melt, and skimming scum on the surface of the melt by using a steel stirring spoon sprayed with the heat-resistant coating after the degassing agent is added;
(5) secondary refining: cooling the melt prepared in the step (4) to 720-730 ℃, adding Ti element into the melt in a wire Al-5Ti-B intermediate alloy mode, and continuously stirring for 15-20 min by using a steel stirring spoon sprayed with heat-resistant coating after adding, wherein the stirring height of the stirring spoon is 1/2-2/3 of the total height of the melt;
(6) blowing degassing and standing treatment: cooling the melt prepared in the step (5) to 685-705 ℃, adding a pure magnesium ingot and a pure lithium ingot into the melt by using a bell jar sprayed with a heat-resistant coating, adding 1/3-1/2 parts with the height of the total height of the melt by using the bell jar, introducing gas into the melt after the pure magnesium ingot and the pure lithium ingot are added, carrying out rotary blowing degassing, and standing the melt for 15-25 min at 710-725 ℃ after the rotary blowing degassing;
(7) casting: adjusting the temperature of the melt to 705-715 ℃, and casting the alloy melt in a sand mold, a metal mold, a gypsum mold or a fired mold shell mold to finish casting of the casting;
(8) electromagnetic induction heating short-time heat treatment: placing the casting in an electromagnetic induction heating furnace, wherein the solid solution heating temperature is 535-550 ℃, the solid solution heating heat preservation time is 6-8 h, and the quenching transfer time is less than or equal to 15 s; the pre-aging heating temperature is 120-140 ℃, and the pre-aging heating heat preservation time is 1.5-3 h; the secondary aging heating temperature is 160-180 ℃, and the secondary aging heating heat preservation time is 4.5-6.0 h.
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